Production of fast-charge Zn-based aqueous batteries via interfacial adsorption of ion-oligomer complexes

Aqueous zinc batteries are attracting interest because of their potential for cost-effective and safe electricity storage. However, metallic zinc exhibits only moderate reversibility in aqueous electrolytes. To circumvent this issue, we study aqueous Zn batteries able to form nanometric interphases at the Zn metal/liquid electrolyte interface, composed of an ion-oligomer complex. In Zn||Zn symmetric cell studies, we report highly reversible cycling at high current densities and capacities (e.g., 160 mA cm−2; 2.6 mAh cm−2). By means of quartz-crystal microbalance, nuclear magnetic resonance, and voltammetry measurements we show that the interphase film exists in a dynamic equilibrium with oligomers dissolved in the electrolyte. The interphase strategy is applied to aqueous Zn||I2 and Zn||MnO2 cells that are charged/discharged for 12,000 cycles and 1000 cycles, respectively, at a current density of 160 mA cm−2 and capacity of approximately 0.85 mAh cm−2. Finally, we demonstrate that Zn||I2-carbon pouch cells (9 cm2 area) cycle stably and deliver a specific energy of 151 Wh/kg (based on the total mass of active materials in the electrode) at a charge current density of 56 mA cm−2.

R eversible electrodeposition of metals has recently reemerged as an area for fundamental and applicationsoriented studies, reviving interest in rechargeable batteries that use metal anodes, such as Lithium (Li), sodium (Na), magnesium (Mg), calcium (Ca), zinc (Zn), and aluminum (Al) [1][2][3][4] . A large body of evidence now exists that uneven, mossy, and dendritic deposits, hinder reversibility in both expected (e.g., limiting battery lifetime through internal shorting) and un-expected (e.g., weakening the connections between deposits and the current collector to promote electronic isolation) ways. In either case, the result is that less of the active metal in the anode is available for charge storage, and consequently few, if any, of the metal anodes under consideration live up to their potential for achieving costeffective and energy-dense storage 5,6 .
These findings have in turn renewed interest in understanding root causes and the fundamental transport and electrochemical processes that promote mossy deposition and dendrite formation over different ranges of current density, i 7,8 . In the low current density region-characterized as current densities well-below the classical diffusion-limited value, i L = 4FcD + /l-classical transportbased theories that invoke hydrodynamic instability 8 are not relevant. Here i L is the limiting current; D + is the cation diffusion coefficient; c the salt concentration in the electrolyte solution (assume to be dilute concentration: ≤0.05 M); l is the space between physically separated electrodes confined in the same cell; and F is Faraday constant. Thus, for i << i L , two processes are thought to be most responsible for non-uniform, wire-like and mossy deposition: (1) uneven electric field lines at irregular deposit features (e.g., bumps, edges, etc.), which promote growth of non-planar wirelike/mossy/dendritic structures 9 ; and (2) uneven charge transport through interphases formed on the metal, leading to preferential nucleation and growth of metal deposits along particular directions. A serious consequence of the second process is that stripping of metal from underneath deposits coated by a nonuniform solid electrolyte interphase, can selectively remove portions of a non-planar deposit near its roots, which promotes breakage and electrochemical disconnection of the deposits (i.e., metal orphaning). This results in high anode irreversibility 10,11 , which typically means the reversible cycling of metal anodes is limited to a few cycles. All of these processes remain at high current density, i → i L , and are augmented by the hydrodynamic instability termed electroconvection, which is driven by an iondepleted, extended space charge layer that extends away from the electrode surface into the bulk 12 . For fundamental reasons discussed elsewhere 13,14 , electroconvection favors localized deposition on a spectrum of length scales and recent studies, including numerical simulation and experimental observation [13][14][15] , show that strong "electroconvection" accelerates growth of non-planar deposit morphologies formed by other processes (Fig. 1a). A consequence is that operation of metal anode batteries is generally limited to the regime i << i L 4, [16][17][18][19][20][21][22] , which is a barrier to their use in electric grid and fast-charging electrified transportation applications where long-term stability at high current densities is demanded.
Aqueous zinc batteries have recently been reported to provide excellent model systems for understanding interfacial processes in all batteries that employ metal anodes 23 . They also promise cost and performance advantages that are attractive from an applications perspective 24,25 . We note however that, notwithstanding the very high D + values in aqueous electrolytes, the highest current density achieved in state-of-the art Zn cells 4 are still substantially below i L (≤40 mA cm −2 ). A number of strategies, including deployment of viscoelastic liquid electrolytes 7 and fieldinduced crystallographic reorientation 8 of Zn deposits have been reported to show potential for suppressing electroconvection and achieving primary smooth, uniform metal electrodeposition at high current densities. These effects are conventionally discussed in terms of coupling between electroconvection (which produces a spatially non-uniform cation flux at the electrode) and secondary flows produced by polymer elasticity or viscous fluid flow produced by electrode motion, either of which can produce counter flows that render the cation flux to the interface more uniform 26,27 . Local Joule heating has been reported as another important strategy to achieve smooth electrodeposition at high current density 28 . Results from linear stability analysis and direct numerical simulations from a number of groups, show that the Damkohler number Da ≡ i 0 /i L , the dimensionless ratio of exchange current i 0 at the electrode to the diffusion-limited current i L in the electrolyte determines the propensity for metals to deposit in largely planar/compact or non-planar/non-compact morphologies 14,26,27,29 . Here we make specific reference to findings from recent direct numerical simulations of coupled electrohydrodynamics, transport, and interfacial reaction of metals at planar interfaces 14,27 , which show that as Da decreases, the lateral gradient of the surface potential creates a lateral ion flux that drives cations away from high cation concentration regions, meaning that the ion velocity (V x ) parallel to the electrode surface increases, while the velocity perpendicular (V y ) decreases (Fig. 1b). This finding is in qualitative accord with reports from direct tracer particle visualization experiments 15,30 , and can be interpreted more simply in terms of a competition between kinetic processes in the following manner: by allowing arriving metal ions sufficient time to redistribute at the electrode surface before they are reduced, low Da values are advantageous for obtaining a smooth electrodeposition morphology, irrespective of the current density. The fast reaction kinetics of metal electroreduction and large volume change at a metal anode required for practical battery operation are fundamental, un-resolved barriers Z z z z z z for creating interphases that support sufficiently low Da at metal anodes in liquid electrolytes, as well as for maintaining such low Da values over long cell lifetimes and under conditions where the anode volume changes significantly during cycles of charge and discharge (Fig. 1b).
Here we report that dynamic, nanometer-thick, ion-oligomer interphases in situ formed on a Zn metal anode inside a singlecell battery provide a powerful and versatile approach for suppressing non-planar deposition by suppressing the full set of instabilities (chemical, morphological, and hydrodynamic) (Fig. 1b). The approach is stable during long-term operation (>10,000 cycles) of an unusually long-time scale (>1000 h). We show further that the spontaneously formed nanolayers enable highly reversible Zn electrodes at current densities as high as 160 mA cm −2 in aqueous electrolytes, which is at the same order of magnitude of the limiting current density (i L ≈ 10^2 mA cm −2 ), and about four times higher than the highest values reported for aqueous Zn electrodes. When paired with conversion cathodes such as I 2 /activated carbon, we demonstrate that the dynamic ion-oligomer complexes enable battery cells, pseudocapacitor-like lifetimes (>12,000 charge/discharge cycles) at high active material utilization. In addition, fast-charge pouch cell batteries employing a 20-μm thin Zn anode are demonstrated to run for over 100 cycles at a charge current density of 56 mA cm −2 . Even without efforts to optimize their performance, the pouch cells achieve specific energy as high as 555 Wh kg −1 AC (151 Wh kg −1 Zn+AC ), illustrating the scalability of the ion-oligomer electrolyte concept. As an extended example, we investigate Zn||MnO 2 aqueous cells and find that they also achieve long-term cycling performance (>1000 charge/discharge cycles) at a charge current density of 160 mA cm −2 , meaning the reported ion-oligomer complexes are quite versatile for both anode and cathode sides (Fig. 1c). We also explore the possibility to apply the in situ formed ion-oligomer nanometric interphase strategy in a non-aqueous electrochemical energy storage system such as an Li||I 2 cell where we demonstrate reversibly battery operation at a current density of 40 mA cm −2 .

Results
As a first step to identifying a general strategy for achieving high metal anode reversibility, we speculate that a conformal, interfacial nanolayer spontaneously formed on a metal electrode by reversible adsorption of poly-/oligo-ethers could simultaneously block electroreduction sites-lowering i 0 -and providing a "selfhealing" (polymer layer can be spontaneously reformed during metal strip and deposit process) characteristic stemming from dynamic polymer adsorption/desorption processes at the electrolyte/electrode interface. To evaluate this hypothesis, we take advantage of the following three well-known effects to create and study adsorption of Zn 2+ -halide ion-oligomer complex at metal substrates: (i) high affinity of metal cations for the lone electron pairs on ether oxygens in poly-ethers; (ii) high surface affinity of halide ions for metal substrates, which has been attributed to their ability to form interfacial halide-metal covalent-like bonds 31 ; and (iii) spontaneous dynamic adsorption/desorption of dissolved polyether ion complexes to the electrode surface. Thus, a welldesigned halide ion-oligoether complex, provides a possible mechanism for reversibly drawing the oligomer out of solution and onto the metal surface, and anchoring it there using strong interfacial bonds between halide and metal. The bonding between Zn 2+ and oligomer increases the de-solvation energy of Zn-ion at the electrode, lowering i 0 for the interfacial reduction of Zn 2+32, 33 . On this basis we speculate that an effective polymer adsorption layer requires a balance between two polymer solution effects: ion-oligomer complex formation and interfacial complex adsorption. The hydrated oligomer must first bond with the initial complexes of Zn 2+ -halide ions in the bulk electrolyte to create the complex, while remaining soluble. The second requirement is that the Zn 2+ -halide ion-oligomer complex dynamically adsorbs onto the surface by the process mentioned above.
Zn 2+ -halide ion-oligomer design and adsorption. We designed and studied the structure of ion-oligomer complexes in aqueous electrolytes formed between Zn 2+ -halide ion complexes and a polyethylene oxide (PEO) oligomer of average molecular weight 300 Da. Aqueous electrolytes solutions based on three zinc halide salts (ZnX 2 (X = Cl, Br, I)) were prepared and the results compared with an aqueous ZnSO 4 reference electrolyte solution. The structure of the solvated Zn halide complexes deduced from Raman vibrational spectroscopy of the electrolytes (Supplementary  Supplementary Fig. 2d). The different initial ion complex states result from the different anion steric structures (SO 4 2− and halide ions) and electronegativity (Cl, Br, I). The LUMO potential of all solvation ions was given by simulation ( Supplementary Fig. 3), which explains the different reaction kinetics (exchange current) in the following sections.
Long-chain PEO (M W > 3000) shows a great potential to regulate Zn electrodeposition due to several reasons 37 : (1) PEO can increase the viscosity of the electrolyte that has a great influence on the ion mobility; (2) due to the interfacial electrode adsorption of PEO, visualization experiments show that the ion velocity V x highly suppressed while V y increases ( Fig. 1b) that may result from the relaxation and contraction of long polymer chain. On the basis of these results, we choose to study polyethylene glycol with a molecular weight of 300 g mol −1 (PEG300). This polymer is of interest because it is easily dissolved in aqueous Zn salt electrolytes to form ion-oligomer complexes. We observed different ion-oligomer complex structures when PEG300 is introduced to the four aqueous Zn salt-based electrolytes.
Nuclear magnetic resonance (NMR) was used to first understand the ion-oligomer complexes formation in aqueous electrolytes containing Zn salts and PEG300. It is known that the deshielding effect results in the left shift of 1 H peak in NMR spectra, therefore, the 1 H peak in the PEG backbone ( Supplementary  Fig. 4) reflects the complexes' stability of PEG300, Zn 2+ , and halide ions. In 5% PEG300 + ZnSO 4 electrolyte, the 1 H peaks of PEG300 shift to the far right, indicating the strong shielding effect here, which increases as the concentration of ZnSO 4 increases (Fig. 2a). We assume that it's the hydrogen bond between Zinc solvation ions, water molecules, and PEG300 that results in this kind of effect, and further predicts the bond model (Fig. 2a). To evaluate our hypothesis, Fourier-transform infrared spectroscopy (FTIR) and ab initio calculations are used to understand the hydrogen bonding effect. In FTIR (Supplementary Figs. 5-7), the ratio between the absorbance intensity of Peak c and Peak d can reflect the level of hydrogen bond cooperativity 38,39 . The value of Peak c/Peak d decreases as 5% PEG is added into the DI water, meaning that much higher hydrogen bonds cooperativity and the interaction between water molecules and PEG is stronger ( Supplementary Fig. 6). 1 M ZnSO 4 salts can further decrease the Peak c/Peak d value, which can be explained by the formation of Zn solvation ions ( Supplementary Fig. 6). An intense decrease of Peak c/Peak d value is observed in the 5% PEG300 + 1 M ZnSO 4 electrolyte, verifying that hydrogen bond is the main factor that facilitates the PEG300- Supplementary Fig. 6). Ab initio calculations further confirms the complex formation model (Supplementary Table 1). However, a different shift trend of the PEG300 1 H peak is observed in Zn halide electrolytes. For ZnCl 2 + 5% PEG electrolytes (Fig. 2b), the shielding effect (peak shift) is not as strong as that of ZnSO 4 electrolyte, indicating lower hydrogen bond cooperativity that can be further confirmed by the increase of Peak c/Peak d value ( Supplementary Fig. 6). Nevertheless, the reverse shifting trend (de-shielding effect) in ZnI 2 + 5% PEG electrolytes indicates a different bonding effect between PEG and the unstable complex [ZnI 3 ]−, [ZnI 2 ] and [ZnI] + , in which no water molecules take part in the ion-oligomer complex formation (Fig. 2c) and the Peak c/Peak d value highly increases ( Supplementary Fig. 7). Such a behavior can be explained by the lower electronegativity and higher polarization of iodine atoms, resulting in a more uniform electron distribution and less partial charge at both Zn and I. Compared to the highly polarized Zn-Cl bond, the [ZnI x ] 2−x complex is less prone to bond with free water (a strong dipole), but prefers bonding with the oxygen atom on PEG, whose partial charge is stabilized by the carbon backbone. The above mechanism is verified in ab initio simulations (Supplementary  Tables 2 and 3). For ZnBr 2 + 5% PEG electrolytes, shielding effect is observed initially (shift to the right) and then overwhelmed by the de-shielding effect (shift back to the left), indicating the ion-oligomer formation effect changes as the concentration of ZnBr 2 increases (Fig. 2d). Bromine has an intermediate electronegativity and polarization compared to chlorine or iodine, and thus demonstrates a mixed behavior of both. On the basis of the 1 H spectrum of NMR results (Fig. 2 (Fig. 2d). All these models are consistent with the ab initio calculations (Supplementary Figs. 8a, b and 9).
The influence of the ion-oligomer complexes on interfacial polymer adsorption was studied using a quartz-crystal microbalance (QCM), ellipsometry, and electrochemical impedance spectroscopy (EIS). QCM (Fig. 3a, b and Supplementary  Fig. 10a-d) is very sensitive to the interfacial polymer adsorption process and can be used to characterize the amount, thickness, reversibility, and interfacial physical properties of the adsorbed polymer layer. We employed three electrolyte flowing steps protocol. First, flowing the blank 1 M ZnSO 4 aqueous electrolyte solution or Zn halide electrolyte solution to establish the effect of salts adsorption on the frequency shift. Second, 5% PEG300 + 1 M ZnSO 4 or Zn halide electrolytes flow through QCM sensor, we can observe the frequency change (Δf) and dissipation change (ΔD) ("dissipation" is the sum of all energy losses in the flowing 3  (2) as shown in Fig. 3b and Supplementary Fig. 10e, the average thickness is related to the interfacial coverage, meaning the thicker the adsorbate layer, the greater the coverage. The designed complex of Zn 2+ -halide ions-PEG300 shows larger interfacial coverage than PEG-[Zn(H2O) 6 ] 2− complex, which we believe reflects the strong interfacial specific adsorption of halide ions 33 ; (3) however, the interfacial viscosity ( Supplementary Fig. 10f) of these four kinds of complexes does not vary greatly, implying that the interfacial viscosity is not the main source of the change of interfacial properties, which disagrees with previous reports 7 ; (4) the ionoligomer adsorption layer is viscoelastic in nature since the shift in different harmonics do not overlap (F_1:3, F_1:5, F_1:7, the number 3, 5, 7 represent the third, fifth and seventh harmonics) and the dissipation values (D_1:3, D_1:5, D_1:7, the number 3, 5, 7 represent the dissipation change for different harmonics) are high (>1 × 10 −6 ). Direct measurement of ion-oligomer complex layer features was performed using an ALPHA-SE Ellipsometer ( Supplementary Fig. 11). These measurements confirm the strong interfacial adsorption of Zn 2+ -halide ions-oligomer complex (Fig. 3c, d). Based on the QCM and ellipsometer results, the adsorbate thickness of the designed ion-oligomer complex varies from 2 to 150 nm, depending on the anion chemistry and polymer concentration. Hence, we can conclude that the influence of the adsorption layer is concentrated in a nanometer-thick interphase zone near the electrode surface.
EIS experiments can also provide complementary insights into the dynamics of an interfacial nanolayer composed of the designed Zn 2+ -halide-PEG300 complex. Figure 4a Table 4 show that much lower interfacial impedance are observed in electrolytes containing ZnI 2 and that these values are reduced slightly in electrolytes containing PEG oligomer additives. These results are consistent with our previous report 33 , which showed the strong interfacial adsorption of unstable iodide and bromide ion complexes facilitate interfacial ion transport. Our earlier results showed further that these complexes are stabilized by adsorption to PEG oligomers, which we believe results in the reduced interfacial impedance observed (Fig. 4d).
Effect of the ion-oligomer complex layer on the Zn electrodeposition. Figure 5 reports the effect of the ion-oligomer complex layer on the Zn electrodeposition process. First, we interrogate the effect of the adsorbed polymer on the exchange   current density (Fig. 5a, b and Supplementary Fig. 13). In all electrolytes studied, the PEG is seen to markedly lower i 0 (Fig. 5b), which we attribute to ion-oligomer adsorption, which can increase the de-solvation energy of Zn 2+ by the aforementioned mechanism. Next, limiting current densities extracted from the current-voltage (i-v) curve ( Supplementary Fig. 14) can further reflect the interfacial ion diffusion kinetics. Zn halide + PEG electrolytes show much higher limiting current densities than ZnSO 4 + PEG electrolytes (Fig. 5c), which results from the strong interfacial adsorption of Zn-halide ion complexes (such as [ZnI 3 ] − ) 33 , further supporting the speculation that halide ions can improve the interfacial adsorption of ion-oligomer complex. Based on these results, we can combine the influence of reaction kinetics and diffusion kinetics by Da (Da ≡ i 0 /i L ). Previous numerical simulations 14,27 show that when Da reaches a critical low value of 0.0025, a uniform ion flux parallels (V y ) at the electrode surface can be achieved. As Shown in Fig. 5d, Da values below this theoretical threshold are observed in ZnBr 2 + PEG300 (Da ≈ 0.0033) and ZnI 2 + PEG300 (Da ≈ 0.0028) electrolytes. Chronoamperometry experiments were performed to more directly correlate the transient current response and electrodeposition morphology under conditions approaching the transport limiting current range. The inflection in the current versus time (i-t) plots for the pure Zn salt and ZnSO 4 + PEG electrolytes is associated with the Sands time (Fig. 5e), indicative of the time-scale required for the space charge to develop and mixing due to formation of electroconvection rolls to begin 8 . The inflection disappears in ZnX 2 (X = Cl, Br, I) + PEG electrolytes ( Fig. 5f-h). Significantly, smooth and uniform Zinc deposits were observed in the ZnBr 2 + PEG and ZnI 2 + PEG electrolytes (Fig. 5i-l), even at current densities in the classical over-limiting electrokinetic regime region (-2.1 V vs AgCl/Ag). Our finding that the Zn electrodeposit morphology is uniform even at the high voltages used in the study implies that it should be possible to create stable Zn batteries able to operate at high current densities as discussed in the following section.
Assembly and testing of aqueous Zn metal lab-scale cells. To evaluate the reversibility of Zn deposits in our designed ionoligomer electrolytes at the high current density, we measured the electrochemical cycling performance of Zn anodes in Zn||carbon cloth half-cell. The plating/stripping Coulombic efficiency (CE %) of Zn deposits in each cycle reveals the ratio between the amount of metal that can be stripped and the amount that is plated in the previous cycle. Figure 6a and Supplementary Fig. 15a show the reversible Coulombic efficiency (CE %) for a long time cycling at current density 160 mA cm −2 and areal capacity 2.6 and 1.1 mAh cm −2 . Compared with ZnI 2 (Supplementary Fig. 15b), ZnSO 4 + PEG300 (Supplementary Fig. 16a) and ZnCl 2 + PEG300 electrolytes (Fig. 6a), ZnBr 2 + PEG300 and ZnI 2 + PEG300 electrolytes (Supplementary Figs. 16b, 17, and 18), show more stable and higher CE (99.2% for ZnBr 2 + PEG and 99.5% for ZnI 2 + PEG, respectively) and better reversible cycling performance (5000 cycles at 2.6 mAh cm −2 and 8000 cycles at 1.1 mAh cm −2 ). It is worth noting that the stable reversible cycling performance at a current density of 160 mA cm −2 was achieved on a Zn anode (Fig. 6).
Benefiting from the long cycle life of the Zn anode at high current density (160 mA cm −2 ), fast-charge aqueous batteries can be produced using ZnI 2 + PEG electrolytes. For ZnI 2 + PEG electrolyte, we choose active carbon (AC) as cathode, which can provide sufficient adsorption site 33 for the oxidation product I 3 − (3I − → I 3 − + 2e − ). Here, to compensate for the relatively low   . Control groups and experimental groups are terminology used throughout the paper to reflect results obtained, respectively, using electrolytes without and with 5% PEG300. The error bars (standard deviations) were calculated based on at least two sets of data.
reaction rate at cathode side, we designed an intermittent charging method for Zn||I 2 (AC) full cell: charging 10 s at 160 mA cm −2 , resting 10 s to enable the interfacial ion equilibrium and then charging another 10 s. As shown in Fig. 6c, voltage increase can be observed in both charging stages, while the voltage drop during the 10-s rest is minimal, demonstrating stable charging behavior. During the discharging process, a stable discharge plateau at 8 mA cm −2 proves the effectiveness of this charge process and the stability of the electrode at ZnI 2 + PEG electrolytes. Significantly, Zn||I 2 (AC) full cell with 1 M ZnI 2 + 5% PEG electrolytes shows stable cycle performance: at a charge current density of 160 mA cm −2 and discharge current density of 8 mA cm −2 , we achieved an areal capacity of 0.88 mAh cm −2 over 12,000 cycles (Fig. 6d), benefiting from the stable Zn electrodeposition and intermittent charging method (Supplementary Fig. 19). Importantly, the designed 1 M ZnI 2 + 5% PEG electrolytes and intermittent charging method can also be applied to pouch cells with 20-μm thick zinc foil (Supplementary Fig. 20). By using ZnI 2 + 5% PEG electrolytes and 20 μm Zn foil, Zn||I 2 (AC) pouch cell can be charged at a high current density of 56 mA cm −2 and run stably over 100 cycles. For pouch cell, we employed a similar intermittent charging method: charge the pouch cell for 1 min at 56 mA cm −2 , then rest for 10 s, and repeat three times (Fig. 6e). Similar to coin cell, a distinct discharge plateau can be observed with discharge current density of 11 mA cm −2 , proving the effectiveness of our ion-oligomer electrolyte system and intermittent charging method. Notably, a specific energy of 555 Wh kg −1 AC at a current of 0.506 A can be achieved based on the mass of AC, and 151 Wh kg −1 can be retained considering the total mass of AC and 20 µm Zn anode (Fig. 6f).
Investigation on the interfacial ion movement mechanism. On the basis of previous simulation results 14,26,27 and our experimental results, we investigated the interfacial ion movement mechanism at the ion-oligomer nanolayer adsorbed on the electrode. Without the ion-oligomer adsorption layer, the high Da value leads to dendrite growth by physical and hydrodynamic instability at high current densities (Fig. 1a). Simulation results show that a viscoelastic polymer coating layer 14,26,27 can regulate the interfacial ion movement by lowering Da (≤0.0025). With a small Da, the interfacial ion movement velocity (V x and V y ) can be regulated as mentioned before and smooth electrodeposition can be achieved. However, considering the mechanical stability of the viscoelastic polymer coating layer, the stagnant coating layer is not suitable for long-term battery cycling. Here, the small Da of "self-healing" dynamic ion-oligomer adsorption layer in ZnBr 2 + PEG300 (Da ≈ 0.0033) and ZnI2+ PEG300 (Da ≈ 0.0028) electrolytes indicate the interfacial ion movement regulation effect also exists here (Fig. 1b). To prove such an effect, we firstly obtained different i-v curves at different concentrations in these four Zn salts (Supplementary Fig. 14). The voltage stability window ΔV extracted from the i-v curve is consistent with the bonding effect and the intensity of the ion-oligomer adsorption layer, proving that the ion movement is influenced by the ion- Furthermore, if the ion movement regulation effect can work well for the Zn anode, the same kind of influence can also work on the intercalation/ de-intercalation cathode at high current density (Fig. 1c). Generally, high current density leads to much more serious problems including electrochemical and hydrodynamic instability for intercalation/de-intercalation cathode materials. Hence, we choose layered MnO 2 cathode 40 (Supplementary Fig. 21) and ZnBr 2 + PEG electrolyte here. The same intermittent charging method for Zn||MnO 2 full cell is applied here: charging 10 s at 160 mA cm −2 , resting 10 s, and then charging another 10 s. The voltage-capacity curve and X-ray diffraction experiments (Fig. 7a, b) show that without regulation of polymer, Zn 2+ is hard to be extracted from MnO 2 cathode at super high current density, which should be the main reason that the MnO 2 is unable to discharge at blank ZnBr 2 electrolyte. However, as shown in Fig. 7c, a slight voltage increase can be observed in both charging stages, demonstrating a potential voltage plateau, while the voltage drop during the 10-s rest is minimal, demonstrating stability. On the other hand, during the discharging process, a stable discharge plateau at 8 mA cm −2 proves the ion movement at cathode sides can also be regulated by the ion-oligomer adsorption layer ( Supplementary Fig. 22 and Fig. 7d). Considering the simplicity and effectiveness of the approach, we wondered whether it could be used to enable fast charging of non-aqueous Li-based batteries. Supplementary  Fig. 23 reports results showing that the concept is effective for lithium-iodine cells. Specifically, we find that Li||I 2 cell that use LiI and 1% PEG300 in a DOL-based electrolyte, can be charged at current densities as high as 40 mA cm −2 ( Supplementary  Fig. 23a). Compared with the electrolyte systems without PEG300 additive (Supplementary Fig. 23b), the LiI + 1% PEG additive can well stabilize the lithium electrodeposition and lead to high Coulombic efficiency (93%) in Li||I 2 cell over 200 cycles (Supplementary Fig. 23c). However, the results reported still need to be further optimized the ion-oligomer complex and electrolyte solvent for Li. Taken together with the more in-depth results for the Zn system, the Li results nonetheless lead us to conclude that the interfacial ion regulation mechanism achieved by the ionoligomer nano-adsorption layer is quite versatile.
In summary, we report that controlling the Zn electrodeposition process at high current density (e.g., 160 mA cm −2 ) can be achieved by an interfacial ion-oligomer interphase with small Damkohler number Da. By designing the Zn 2+ -halide ion-PEG complex, reversible interfacial ion-oligomer adsorption can meet both the experimental and theoretical requirements (small Da). Small Da indicates that the ion-oligomer adsorption layer can effectively regulate the interfacial ion movement, and this kind of ion regulation effect can be applied to both anode and cathode sides. More importantly, a highly reversible Zn anode at a high current density of 160 mA cm −2 enables the fast-charge aqueous coin cell with noticeable stability (160 mA cm −2 , 12,000 cycles) and fast-charge pouch cell with good cycling performance (56 mA cm −2 , over 100 cycles) ( Supplementary Fig. 24). Finally, we perform initial proof of concept studies to show that the findings are also relevant for achieving reversible, fast charge characteristics at reactive metal electrodes like Li tested in nonaqueous electrolyte environment.
For Li-containing non-aqueous electrolyte solution, 2 M LiTFSI, 0.5 M LiNO 3 and 1 M LiI were added to the DOL solvent. For polymer-containing electrolyte, 1 wt% PEG400 was added.
Electrochemical measurements. Galvanostatic charge/discharge performance of coin cells were tested on Neware battery test systems at room temperature (25 ± 1°C). No climatic/environmental chamber was used. Electrochemical studies were performed using CR2032 coin cells. The area of electrodes in this study is 0.3175 cm 2 . Half cells were assembled with 0.25 mm Zn foil and carbon cloth and separated by a glass fiber (GF/A, WHA1821047, thickness 0.68 mm, pore size 1 μm). In each coil cell,~100 μL electrolyte was added by pipette.
In the Zn||I 2 -AC coin cell, the electrolyte was 1 M ZnI 2 with/without 5 wt.% PEG300. The cathode is prepared by mixing AC, Super P carbon and polyvinylidene fluoride at a weight ratio 8:1:1. The mass loading of AC is 5 mg cm −2 . In the Zn|| MnO 2 coin cell, α-MnO 2 was synthesized via a conventional hydrothermal route, in which a solution that contains 5 mM KMnO 4 and 0.3 M HCl was kept at 140°C for 18 h. All coin cells were assembled at the air.
For pouch cell, 20-μm zinc foil was assembled with cathode materials and separated by a Celgard 3501 membrane. Single-layer electrode was used in pouch cell. The area of the electrode is 9 cm 2 . The pouch cells were assembled in Ar-filled glovebox. The specific energy of pouch cell was calculated by: Specific energy Wh kg À1 À Á ¼ Average discharge voltage V ð Þ discharge capacityðAhÞ Total mass ðkg; active materials on cathode side þ Zn anodeÞ For Li||I 2 -AC cell, all procedures are the same as Zn||I 2 -AC cell. The electrolyte is DOL + 2 M LiTFSI + 2 M LiI + 0.5 M LiNO 3 + 1% PEG400 and the membrane is Celgard 2400. The cathode side is AC. The Li||I 2 -AC cell was assembled in Arfilled glovebox.
EIS measurements was performed using a Solartron in a frequency range from 50 to 1 HZ with an AC polarization of 10 mV. The measurements used twoelectrode zinc symmetric cells. Overall, 56 points were collected for each test. Before carrying out the EIS measurement, the open-circuit voltage-time applied was 2 h.
For i-v curve, a three-electrode system, including a working electrode made of glassy carbon, a counter electrode made of zinc foils and a reference electrode (AgCl/Ag), was used to measure the i-v curve of these four zinc salts electrolyte with various concentration (0.05 M, 0.5 M and 1 M). The glassy carbon electrode was purchased from Pine Research. The scan rate of all experiments is 5 mV s −1 . Limiting current can be extracted from the i-v curve. During the scanning process, no bubbling is observable near the working electrode, which is attributable to the sluggish kinetics of the H 2 evolution reaction in this system.
Exchange current: cyclic voltammetry was performed using a CHI 600E electrochemical workstation and symmetrical zinc cells, in which the glass fiber is   For Ellipsometer experiments, a silicon wafer with a 2 × 2 cm 2 area was used. For each silicon wafer, we tested three points and get the average thickness. For each kind of electrolyte, we tested three samples (three silicon wafers), which means totally we tested nine times for the PEG adsorption thickness and then extracted the average value.
Field-emission scanning electron microscopy was carried out on Zeiss Gemini 500 Scanning Electron Microscope equipped with Bruker energy dispersive spectroscopy detector to study the electrodeposition morphology of Zn. NMR 1 H spectra were collected on a Bruker AVIIIHD (H, 500 MHz) spectrometer with a broad band Prodigy cryoprobe and referenced to D 2 O solvent shifts (D 2 O = 4.78 ppm). Linear sweep voltammetry was performed using a CH 600E electrochemical workstation. Impedance measurements of all electrolytes were measured using frequency-domain dielectric relaxation measurements in the range 10 7 -10 −1 Hz using a Novocontrol Broadband dielectric spectrometer. ATR-FTIR spectra were conducted using a Thermo Scientific spectrometer. Renishaw inVia confocal Raman microscope is used for Raman tests of electrolytes (excitation wave-length: 785 nm).
QCM-D measurements were performed with Q-sense Explorer system (Biolin Scientific AB) at 25°C. Fundamental frequency and three harmonics (third, fifth and seventh) were recorded simultaneously along with the corresponding dissipation factors. Gold coated AT-cut quartz crystal (fundamental frequencỹ 4.95 MHz) was purchased from Q-sense (QX301). Before the experiment, the crystal was cleaned by immersing in 5:1:1 solution of water, ammonia (25%) and hydrogen peroxide (30%) for 5 min at 75°C, followed by thorough rinsing with deionized water. The crystal was subsequently dried with nitrogen gas and finally UV treated for 10 min in UV/Ozone Procleaner TM (Bioforce, Nanosciences). 1 M ZnSO 4 and Zn halide solution was used as the buffer solution and a stable baseline was obtained before switching to 1 M ZnSO 4 and Zn halide solution + 5 wt% PEG300 solution. The data obtained from QCM-D was modeled using the Q-tools software (Q-sense). "Voigt" viscoelastic model was used to model third, fifth and seventh harmonics. This model assumes a homogeneous adsorbed layer. Fluid density and viscosity were taken to be 1638 kg m −3 and 0.001 kg ms −1 , respectively. The density of the adsorbed layer was assumed to be 1125 kg m −3 (which is the density of the PEG300) for calculating viscoelastic properties. Descending incremental fitting was used. Direct measurement of ion-oligomer complex adsorption thickness was performed at ALPHA-SE ELLIPSOMETER. The data were collected through three angles (65°, 70°, 75°) and ten different adsorption sites of the silicon wafer, and then get the average adsorption thickness of different PEG300+ Zn salts electrolytes.
First-principles calculations. The bond formation of PEG-Zn-halide complexes was studied by ab initio quantum chemistry calculations using the General Atomic and Molecular Electronic Structure System (GAMESS-US), version 2019 R1 patch 1. All calculations were based on the restricted Hartree-Fork method, with a non-SMD solvation model of water (ε = 78.3553) and a gradient convergence tolerance of 0.0001 Hartree Bohr -1 . An example of our GAMESS header can be found below. The initial geometries of the ZnX n (H 2 O) m−n complexes were individually constructed in Avogadro ver1.2.0 and then optimized in GAMESS using a 6-31G** basis set assuming the atomic radius of Zn is 1.39 Å. Together with a linear PEG molecule and five free water molecules, each ZnX n (H 2 O) m−n complex structure was further optimized in GAMESS using the same parameter settings. The degree of polymerization of PEG was chosen to be 5-unit to resemble the molecular weight used in the experiment (~300 g mol −1 ). After convergence, the bond lengths and bond angles were obtained from the equilibrium structure. HOMO and LUMO energy extracted from the ab initio model.

Data availability
All datasets generated and analyzed during the current study are available from the corresponding author upon reasonable request.